Nonaqueous electrolyte battery containing a negative electrode of lithium-titanium composite oxide, battery pack and vehicle

ABSTRACT

A nonaqueous electrolyte battery, containing a case and provided in the case, a positive electrode, a negative electrode and a nonaqueous electrolyte. The negative electrode comprises a lithium-titanium composite oxide, wherein a crystallite diameter of the lithium-titanium composite oxide is not larger than 6.9×10 2  Å. The lithium-titanium composite oxide comprises: rutile TiO 2 ; anatase TiO 2 ; Li 2 TiO 3 ; and a lithium titanate having a spinel structure. A main peak intensity relative to lithium titanate set at 100, as determined by X-ray diffractometry, of each of lithium titanate having a spinel structure, the rutile TiO 2 , the anatase TiO 2  and Li 2 TiO 3  is not larger than 7.

CROSS-REFERENCE TO RELATED APPLICATIONS

This application is a continuation application of U.S. patentapplication Ser. No. 12/512,540, filed Jul. 30, 2009, the disclosure ofwhich is incorporated herein by reference in its entirety. The parentapplication is a continuation application of U.S. patent applicationSer. No. 11/228,430, filed Sep. 19, 2005, now U.S. Pat. No. 7,595,134,issued Sep. 29, 2009, the disclosure of which is incorporated herein byreference in its entirety. The parent application claims priority toJapanese Patent Application No. 2005-141146, filed May 13, 2005, thedisclosure of which is incorporated herein by reference in its entirety.

BACKGROUND OF THE INVENTION

1. Field of the Invention

The present invention relates to a nonaqueous electrolyte battery, alithium-titanium composite oxide, a battery pack and a vehicle.

2. Description of the Related Art

A vigorous research is being conducted on a nonaqueous electrolytebattery having a high energy density in which lithium ions are migratedbetween the negative electrode and the positive electrode for chargingand discharging the battery.

Various properties are required for the nonaqueous electrolyte batterydepending on the use of the battery. For example, the discharge under acurrent of about 3 C is expected when the nonaqueous electrolyte batteryis used in a digital camera, and the discharge under a current of atleast about 10 C is expected when the nonaqueous electrolyte battery isused in a vehicle such as a hybrid electric automobile. Such being thesituation, the large current characteristics are particularly requiredin the nonaqueous electrolyte battery used in the technical fieldsexemplified above.

Nowadays, a nonaqueous electrolyte battery in which a lithium-transitionmetal composite oxide is used as a positive electrode active materialand a carbonaceous material is used as a negative electrode activematerial has been put to the practical use. In general, Co, Mn or Ni isused as the transition metal included in the lithium-transition metalcomposite oxide.

In recent years, a nonaqueous electrolyte battery in which alithium-titanium composite oxide having a high Li absorption-releasepotential relative to the carbonaceous material has been put to thepractical use. Since the lithium-titanium composite oxide is small inthe change of volume accompanying the charge-discharge of the battery,the lithium-titanium composite oxide is expected to improve thecharge-discharge cycle characteristics of the secondary battery.

Among the lithium-titanium composite oxides, the Spinel type lithiumtitanate is expected to be particularly useful. The Spinel type lithiumtitanate can be synthesized by, for example, mixing lithium hydroxidewith titanium dioxide, followed by baking the resultant mixture. If thebaking is insufficient in this synthesizing process, obtained arelithium-titanium composite oxides containing an anatase type TiO₂, arutile type TiO₂, and Li₂TiO₃ as impurity phases in addition to theSpinel type lithium titanate.

It is disclosed in Japanese Patent Disclosure (Kokai) No. 2001-240498that lithium-titanium composite oxides containing the Spinel typelithium titanate as a main component, having a small amount of theimpurity phases noted above, and also having a crystallite diameter of700 to 800 Å can be used as the negative electrode active materialhaving a large capacity.

BRIEF SUMMARY OF THE INVENTION

An object of the present invention is to provide a nonaqueouselectrolyte battery, a lithium-titanium composite oxide, a battery packand a vehicle, which are excellent in the large current characteristics.

According to a first aspect of the present invention, there is provideda nonaqueous electrolyte battery, comprising:

a case;

a positive electrode provided in the case;

a negative electrode provided in the case and containing alithium-titanium composite oxide comprising a crystallite diameter notlarger than 6.9×10² Å, the lithium-titanium composite oxide a rutiletype TiO₂, an anatase type TiO₂, Li₂TiO₃ and a lithium titanate having aspinel structure, the rutile type TiO₂, the anatase type TiO₂ andLi₂TiO₃ each having a main peak intensity not larger than 7 on the basisthat a main peak intensity of the lithium titanate as determined by theX-ray diffractometry is set at 100; and

a nonaqueous electrolyte provided in the case.

According to a second aspect of the present invention, there is provideda battery pack comprising nonaqueous electrolyte batteries,

each of the nonaqueous electrolyte batteries comprising:

a case;

a positive electrode provided in the case;

a negative electrode provided in the case and containing alithium-titanium composite oxide comprising a crystallite diameter notlarger than 6.9×10² Å, the lithium-titanium composite oxide including arutile type TiO₂, an anatase type TiO₂, Li₂TiO₃ and a lithium titanatehaving a spinel structure, the rutile type TiO₂, the anatase type TiO₂and Li₂TiO₃ each having a main peak intensity not larger than 7 on thebasis that a main peak intensity of the lithium titanate as determinedby the X-ray diffractometry is set at 100; and

a nonaqueous electrolyte provided in the case.

Further, according to a third aspect of the present invention, there isprovided a lithium-titanium composite oxide comprising a crystallitediameter not larger than 6.9×10² Å, the lithium-titanium composite oxideincluding a rutile type TiO₂, an anatase type TiO₂, Li₂TiO₃ and alithium titanate having a spinel structure, the rutile type TiO₂, theanatase type TiO₂ and Li₂TiO₃ each having a main peak intensity notlarger than 7 on the basis that a main peak intensity of the lithiumtitanate as determined by the X-ray diffractometry is set at 100.

According to a fourth aspect of the present invention, there is provideda vehicle comprising a battery pack comprising nonaqueous electrolytebatteries,

each of the nonaqueous electrolyte batteries comprising:

a case;

a positive electrode provided in the case;

a negative electrode provided in the case and containing alithium-titanium composite oxide comprising a crystallite diameter notlarger than 6.9×10² Å, the lithium-titanium composite oxide including arutile type TiO₂, an anatase type TiO₂, Li₂TiO₃ and a lithium titanatehaving a spinel structure, the rutile type TiO₂, the anatase type TiO₂and Li₂TiO₃ each having a main peak intensity not larger than 7 on thebasis that a main peak intensity of the lithium titanate as determinedby the X-ray diffractometry is set at 100; and

a nonaqueous electrolyte provided in the case.

BRIEF DESCRIPTION OF THE SEVERAL VIEWS OF THE DRAWING

FIG. 1A is a cross sectional view schematically showing as an examplethe construction of a unit cell according to a first embodiment of thepresent invention;

FIG. 1B is a cross sectional view schematically showing the constructionof the circular portion A shown in FIG. 1A;

FIG. 2 is an oblique view showing in a dismantled fashion theconstruction of a battery pack according to a second embodiment of thepresent invention;

FIG. 3 is a block diagram showing the electric circuit of the batterypack according to the second embodiment of the present invention;

FIG. 4 is a graph showing the X-ray diffraction pattern of thelithium-titanium composite oxide for the Example of the presentinvention;

FIG. 5 is an oblique view, partly broken away, schematically showing theconstruction of another unit cell according to the first embodiment ofthe present invention; and

FIG. 6 is a cross sectional view showing in a magnified fashion theconstruction of the circular portion B shown in FIG. 5.

DETAILED DESCRIPTION OF THE INVENTION

As a result of an extensive research, the present inventors have foundthat the lithium-titanium composite oxide exhibits a relatively lowlithium ion conductivity. For example, it has been found that thelithium ion conductivity of the lithium-titanium composite oxide is muchlower than that of lithium-cobalt composite oxide. To be more specific,the lithium ion conductivity of the lithium-titanium composite oxide isone-several hundredth of that of lithium-cobalt composite oxide. As aresult, in the nonaqueous electrolyte battery comprising bothlithium-titanium composite oxide and lithium-cobalt composite oxide, thediffusion of the lithium ions in the lithium-titanium composite oxideprovides the rate-determining step and thus, the nonaqueous electrolytebattery is made poor in its large current characteristics.

Under the circumstances, the present inventors have found that thediffusion rate of the lithium ions is increased with decrease in thecrystallite diameter of the lithium-titanium composite oxide so as toimprove the ionic conductivity of the lithium-titanium composite oxide.

The present inventors have also found that the diffusion rate of lithiumions is increased with decrease in the amount of the impurity phasescontained in the lithium-titanium composite oxide. It is consideredreasonable to understand that the impurity phases impair the diffusionof lithium ions so as to lower the diffusion rate of the lithium ions.

However, where the baking is performed sufficiently in the manufacturingprocess, the lithium-titanium composite oxide has a large crystallitediameter and the amount of the impurity phases is decreased in themanufactured lithium-titanium composite oxide. On the other hand, wherethe baking is suppressed in the manufacturing process, thelithium-titanium composite oxide has a small crystallite diameter andcontains a large amount of the impurity phases. Such being thesituation, it was difficult to manufacture a lithium-titanium compositeoxide having a small crystallite diameter and containing a small amountof the impurity phases so as to make it difficult to improve the ionicconductivity of the lithium-titanium composite oxide.

The present inventors have found that the ionic conductivity of thelithium-titanium composite oxide can be improved by allowing thecrystallite diameter and the amount of the impurity phases of thelithium-titanium composite oxide to satisfy the conditions describedherein later, thereby improving the large current dischargecharacteristics of the nonaqueous electrolyte battery.

Each embodiment of the present invention will now be described withreference to the accompanying drawings. Incidentally, in theaccompanying drawings, the common constituents of the embodiment aredenoted by the same reference numerals so as to omit the overlappingdescription. Also, the accompanying drawings are schematic drawings thatare simply intended to facilitate the understanding of the presentinvention. The accompanying drawings may include portions differing fromthe actual apparatus in the shape, size and ratio. However, the designof the apparatus may be changed appropriately in view of the followingdescription and the known technologies.

FIRST EMBODIMENT

The construction of the unit cell as an example according to the firstembodiment of the present invention will now be described with referenceto FIGS. 1A and 1B. Specifically, FIG. 1A is a cross sectional viewschematically showing the construction of a flattened type nonaqueouselectrolyte secondary battery according to the first embodiment of thepresent invention, and FIG. 1B is a cross sectional view showing indetail the construction of a circular region A shown in FIG. 1A.

A positive electrode terminal 1 is electrically connected to a positiveelectrode 3, and a negative electrode terminal 2 is electricallyconnected to a negative electrode 4. The positive electrode 3, thenegative electrode 4 and a separator 5 interposed between the positiveelectrode 3 and the negative electrode 4 collectively form a flattenedwound electrode 6. Since the separator 5 is interposed between thepositive electrode 3 and the negative electrode 4, the negativeelectrode 4 and the positive electrode 3 are positioned spatially apartfrom each other. The wound electrode 6 is housed in a case 7 having anonaqueous electrolyte loaded therein.

As shown in FIG. 1A, the flattened wound electrode 6 is housed in thecase 7 having the nonaqueous electrolyte loaded therein. The negativeelectrode 2 is electrically connected to the outside and the positiveelectrode terminal 1 is electrically connected to the inside in thevicinity of the outer circumferential edge of the wound electrode 6. Thewound electrode 6 has a laminate structure comprising the negativeelectrode 4, the separator 5, the positive electrode 3 and the separator5, which are laminated one upon the other in the order mentioned, thoughthe laminate structure is not shown in FIG. 1A.

FIG. 1B shows more in detail the construction of the wound electrode 6.As shown in the drawing, the positive electrode 3, the negativeelectrode 4 and the separator 5 interposed between the positiveelectrode 3 and the negative electrode 4 are laminated one upon theother in the order mentioned. The negative electrode 4 constituting theoutermost circumferential region comprises a negative electrode currentcollector 4 a forming the outer layer and a negative electrode layer 4 bpositioned inside the negative electrode current collector 4 a . Each ofthe other negative electrodes 4 comprises the negative electrode layer 4b , the negative electrode current collector 4 a and the additionalnegative electrode layer 4 b, which are laminated one upon the other inthe order mentioned. Likewise, the positive electrode 3 comprises apositive electrode layer 3 b, a positive electrode current collector 3 aand another positive electrode layer 3 b, which are laminated one uponthe other in the order mentioned.

The negative electrode, the nonaqueous electrolyte, the positiveelectrode, the separator, the case, the positive electrode terminal, andthe negative electrode terminal included in the nonaqueous electrolytebattery will now be described in detail.

1) Negative Electrode

The negative electrode comprises a negative electrode current collectorand a negative electrode layer supported on one surface or both surfacesof the negative electrode current collector and containing a negativeelectrode active material, a negative electrode conductive agent, and abinder.

The negative electrode active material comprises a lithium-titaniumcomposite oxide having the crystallite diameter not larger than 6.9×10²Å and containing a lithium titanate having a spinel structure(hereinafter referred to a Spinel type lithium titanate) as the maincomponent and low in the impurity phase content. The Spinel type lithiumtitanate can be represented by the chemical formulaLi_(4+x)Ti₅O₁₂(0≦x≦3).

To be more specific, the crystallite diameter of the lithium-titaniumcomposite oxide, which is obtained by the Scherrer formula from the halfvalue width of the X-ray diffraction peak, is not larger than 6.9×10² Å.Also, the lithium-titanium composite oxide contains a rutile type TiO₂,an anatase type TiO₂ and Li₂TiO₃ each having the main peak intensity notlarger than 7 on the basis that the main peak intensity of the Spineltype lithium titanate as determined by the X-ray diffractometry is setat 100. Incidentally, the situation that the main peak intensity of anyof the rutile type TiO₂, the anatase type TiO₂ and Li₂TiO₃ is not largerthan 7 covers the case where the main peak intensity is zero (0) in someof the main peak intensity of the rutile type TiO₂, the main peakintensity of the anatase type TiO₂ and the main peak intensity ofLi₂TiO₃, and the case where the main peak intensity is zero in all ofthe rutile type TiO₂, the anatase type TiO₂ and Li₂TiO₃. Where the mainpeak intensity is lower than the detection limit, the main peakintensity is regarded as being zero (0).

The main peak of the Spinel type lithium titanate denotes the peak inthe case where the lattice spacing d in the X-ray diffraction pattern is4.83 Å. Also, the main peak of the anatase type TiO₂, the main peak ofthe rutile type TiO₂ and the main peak of Li₂TiO₃ denote the peaks inthe cases where the lattice spacing d is 3.51 Å, 3.25 Å and 2.07Å,respectively.

The lithium-titanium composite oxide in this embodiment of the presentinvention makes it possible to increase the diffusion rate of thelithium ions and to improve the ionic conductivity. In addition, it ispossible to improve the large current characteristics of the nonaqueouselectrolyte battery. Incidentally, the diffusion rate noted aboveincludes both the transgranular diffusion and the grain boundarydiffusion. It is considered reasonable to understand that the effectproduced by the lithium-titanium composite oxide according to thisembodiment of the present invention is produced by the situation thatthe lithium ion diffusion rate at the crystal grain boundary is higherthan that inside the crystal grain.

It is desirable for the crystallite diameter of the lithium-titaniumcomposite oxide to be not larger than 5.3×10² Å. If the crystallitediameter is not larger than 5.3×10² Å, the ionic conductivity and thelarge current characteristics can be further improved. It is moredesirable for the crystallite diameter to be not larger than 4.4×10² Å.

It is desirable for the crystallite diameter of the lithium-titaniumcomposite oxide to be not smaller than 1.5×10² Å. If the crystallitediameter is not smaller than 1.5×10² Å, it is possible to form easilythe lithium-titanium composite oxide low in the contents of the impurityphases such as the rutile type TiO₂, the anatase type TiO₂ and Li₂TiO₃.It is more desirable for the crystallite diameter to be not smaller than2.6×10² Å.

It is desirable for the main peak intensity of any of the rutile typeTiO₂, the anatase type TiO₂ and Li₂TiO₃ to be not higher than 3, moredesirably not higher than 1.

The diffusion rate of the lithium ions can be further improved withdecrease in the amount of the impurity phases noted above. Also, theionic conductivity and the large current characteristics can be improvedwith decrease in the amount of the impurity phases noted above.

It is desirable for the lithium-titanium composite oxide to be in theform of particles having the average particle diameter not smaller than100 nm and not larger than 1 μm. If the average particle diameter is notsmaller than 100 nm, the lithium-titanium composite oxide can be handledeasily in the industrial manufacture of the nonaqueous electrolytebattery. Also, if the average particle diameter is not larger than 1 μm,the diffusion of the lithium ions within a particle can be performedsmoothly.

It is desirable for the lithium-titanium composite oxide to have aspecific surface area not smaller than 5 m²/g and not larger than 50m²/g. If the specific surface area is not smaller than 5 m²/g, it ispossible to secure sufficiently the absorption-release sites of thelithium ions. On the other hand, if the specific surface area is notlarger than 50 m²/g, the lithium-titanium composite oxide can be handledeasily in the industrial manufacture of the nonaqueous electrolytebattery.

Incidentally, it is possible for the lithium-titanium composite oxide tocontain Nb, Pb, Fe, Ni, Si, Al, Zr, etc. in an amount of 1,000 ppm orless.

An example of the manufacturing method of the lithium-titanium compositeoxide will now be described.

In the first step, prepared is a lithium salt used as a lithium sourcesuch as lithium hydroxide, lithium oxide or lithium carbonate. Alsoprepared are a sodium hydroxide as the sodium source and potassiumhydroxide as the potassium source. Prescribed amounts of the lithiumsource and at least one of the sodium source and potassium source aredissolved in a pure water so as to obtain an aqueous solution. Desiredaddition amounts of the sodium source and the potassium source will bedescribed herein later.

In the next step, titanium oxide is put in the resultant solution suchthat lithium and titanium have a prescribed atomic ratio. For example,in the case of synthesizing the lithium-titanium composite oxide havingthe spinel structure and the chemical formula of Li₄Ti₅O₁₂, titaniumoxide is added to the solution such that Li and Ti have an atomic ratioof 4:5.

In the next step, the solution thus obtained is dried while stirring thesolution so as to obtain a baking precursor. The drying method employedin this stage includes, for example, a spray drying, a granulatingdrying, a freeze drying, and a combination thereof. The baking precursorthus obtained is baked so as to form a lithium-titanium composite oxidefor this embodiment of the present invention. It suffices to perform thebaking under the air atmosphere. It is also possible to perform thebaking under an oxygen gas atmosphere or an argon gas atmosphere.

It suffices to perform the baking under temperatures not lower than 680°C. and not higher than 1,000° C. for about 1 hour to about 24 hours.Preferably, the baking should be carried out under temperatures notlower than 720° C. and not higher than 800° C. for 5 hours to 10 hours.

If the baking temperature is lower than 680° C., the reaction betweentitanium oxide and the lithium compound is rendered insufficient so asto increase the amount of the impurity phases such as the anatase typeTiO₂, the rutile type TiO₂ and Li₂TiO₃, with the result that theelectric capacity is decreased. On the other hand, if the bakingtemperature exceeds 1,000° C., the sintering of the Spinel type lithiumtitanate proceeds so as to cause the crystallite diameter to beincreased excessively and, thus, to lower the large current performance.

The lithium-titanium composite oxide manufactured by the manufacturingmethod described above contains Na or K. Each of Na and K performs thefunction of suppressing the crystal growth of the Spinel type lithiumtitanate. Such being the situation, it is possible to suppress thegrowth of the crystallite of the Spinel type lithium titanate even ifthe baking is performed under high temperatures in an attempt to preventthe phases such as the anatase type TiO₂, the rutile type TiO₂ andLi₂TiO₃ from remaining unreacted. As a result, it is possible to obtainthe lithium-titanium composite oxide having a small crystallite diameterand low in the impurity phase content. It should also be noted thatsince the lithium-titanium composite oxide contains an element Xconsisting of at least one of Na and K, the stability of the crystalstructure is enhanced so as to improve the charge-discharge cyclecharacteristics of the nonaqueous electrolyte battery. Also, it ispossible to improve the ionic conductivity of the lithium-titaniumcomposite oxide.

It is desirable for the lithium-titanium composite oxide to contain theelement X, i.e., (Na+K), in an amount not smaller than 0.10% by weightand not larger than 3.04% by weight based on the amount of thelithium-titanium composite oxide. If the amount of (Na+K) contained inthe lithium-titanium composite oxide is smaller than 0.10% by weight, itis difficult to obtain a sufficient effect of suppressing the crystalgrowth. It is also difficult to obtain a sufficient effect ofstabilizing the crystal structure and of improving the ionicconductivity. On the other hand, if the amount of (Na+K) is larger than3.04% by weight, it is possible for the Spinel type lithium titanatecontaining Na and K to form an impurity phase so as to lower theelectric capacity of the nonaqueous electrolyte battery. It should benoted in this connection that the phenomenon noted above is broughtabout because Li is possibly substituted by the element X and theelement X can be positioned in the sites of Li of the Spinel typelithium titanate.

It is possible for each of Na and K to be positioned in the Li sites ofthe Spinel type lithium titanate. This can be confirmed by applying anX-ray diffraction measurement to the lithium-titanium composite oxide soas to perform the Rietveld analysis. For performing the Rietveldanalysis, it is possible to use, for example, RIETAN (trade name of ananalytical soft ware). If Na or K is positioned in the Li site of theSpinel type lithium titanate, the stability of the crystal structure canbe further improved and, at the same time, the segregation can besuppressed.

It is desirable for the lithium-titanium composite oxide to contain K inan amount larger than that of Na because K produces a higher effect ofpromoting the crystallization and, thus, permits shortening thesintering time.

Incidentally, it is possible to use titanium oxide containing aprescribed amount of Na or K as the raw material in the manufacturingprocess in place of allowing sodium hydroxide and/or potassium hydroxideto be dissolved in water.

It is possible to use, for example, acetylene black, carbon black,graphite, etc. as the negative electrode conductive agent for enhancingthe current collecting performance and for suppressing the contactresistance between the current collector and the active material.

It is possible to use, for example, polytetrafluoroethylene (PTFE),polyvinylidene fluoride (PVdF), a fluorinated rubber, astyrene-butadiene rubber, etc. as the binder for bonding the negativeelectrode active material to the negative electrode conductive agent.

Concerning the mixing ratio of the negative electrode active material,the negative electrode conductive agent, and the binder, it is desirablefor the negative electrode active material to be used in an amount notsmaller than 70% by weight and not larger than 96% by weight, for thenegative electrode conductive agent to be used in an amount not smallerthan 2% by weight and not larger than 28% by weight, and for the binderto be used in an amount not smaller than 2% by weight and not largerthan 28% by weight. If the mixing amount of the negative electrodeconductive agent is smaller than 2% by weight, the current collectingperformance of the negative electrode layer may be lowered so as topossibly lower the large current characteristics of the nonaqueouselectrolyte battery. Also, if the mixing amount of the binder is smallerthan 2% by weight, the bonding between the negative electrode layer andnegative electrode current collector may be lowered so as to possiblylower the charge-discharge cycle characteristics of the nonaqueouselectrolyte battery. On the other hand, it is desirable for the mixingamount of each of the negative electrode conductive agent and the binderto be not larger than 28% by weight in view of the improvement in thecapacity of the nonaqueous electrolyte battery.

It is desirable for the negative electrode current collector to beformed of an aluminum foil that is electrochemically stable within thepotential range nobler than 1.0 V or an aluminum alloy foil containingan element such as Mg, Ti, Zn, Mn, Fe, Cu, or Si.

The negative electrode can be prepared by, for example, coating anegative electrode current collector with a slurry prepared bysuspending a negative electrode active material, a negative electrodeconductive agent and a binder in a solvent, followed by drying thecoated slurry so as to form a negative electrode layer on the negativeelectrode current collector and subsequently pressing the currentcollector having the negative electrode layer formed thereon.Alternatively, it is also possible to form a mixture of a negativeelectrode active material, a negative electrode conductive agent and abinder into pellets for forming a negative electrode layer.

2) Nonaqueous Electrolyte

The nonaqueous electrolyte includes a liquid nonaqueous electrolyte thatis prepared by dissolving an electrolyte in an organic solvent and agel-like nonaqueous electrolyte that is prepared by using a compositematerial containing a liquid nonaqueous electrolyte and a polymermaterial.

The liquid nonaqueous electrolyte can be prepared by dissolving anelectrolyte in an organic solvent in a concentration not lower than 0.5mol/L and not higher than 2.5 mol/L.

The electrolyte includes, for example, lithium salts such as lithiumperchlorate (LiClO₄), lithium hexafluoro phosphate (LiPF₆), lithiumtetrafluoro borate (LiBF₄), lithium hexafluoro arsenate (LiAsF₆),lithium trifluoro metasulfonate (LiCF₃SO₃), bistrifluoromethyl sulfonylimide lithium [LiN(CF₃SO₂)₂], and a mixture thereof. It is desirable touse an electrolyte that is unlikely to be oxidized under a highpotential. Particularly, it is most desirable to use LiPF₆ as theelectrolyte.

The organic solvent includes, for example, cyclic carbonates such aspropylene carbonate (PC), ethylene carbonate (EC) and vinylenecarbonate; linear carbonates such as diethyl carbonate (DEC), dimethylcarbonate (DMC) and methyl ethyl carbonate (MEC); cyclic ethers such astetrahydrofuran (THF), 2-methyl tetrahydrofuran (2Me THF) and dioxolane(DOX); linear ethers such as dimethoxy ethane (DME), and diethoxy ethane(DEE); as well as γ-butyrolactone (GBL), acetonitrile (AN) and sulfolane(SL). These solvents can be used singly or in the form of a mixedsolvent.

The polymer materials include, for example, polyvinylidene fluoride(PVdF), polyacrylonitrile (PAN) and polyethylene oxide (PEO).

It is desirable to use a mixed solvent prepared by mixing at least twoorganic solvents selected from the group consisting of propylenecarbonate (PC), ethylene carbonate (EC) and γ-butyrolactone (GBL).Further, it is more desirable to use the organic solvent containingγ-butyrolactone (GBL).

It should be noted that the lithium-titanium composite oxide permitsabsorbing-releasing lithium ions in the potential region in the vicinityof 1.5V (vs. Li/Li⁺). However, in the potential region noted above, thenonaqueous electrolyte is unlikely to be decomposed by reduction, and afilm consisting of the reduction product of the nonaqueous electrolyteis unlikely to be formed on the surface of the lithium-titaniumcomposite oxide. Such being the situation, if the nonaqueous electrolytebattery is stored under the state that lithium ions have been inserted,i.e., under the charged state, the lithium ions inserted in thelithium-titanium composite oxide are gradually diffused into the liquidelectrolyte so as to bring about a so-called “self-discharge”. Theself-discharge is rendered prominent with increase in the temperature ofthe storing environment of the battery.

As described above, the lithium-titanium composite oxide in thisembodiment of the present invention has a small crystallite diameter soas to increase the crystal boundary area per unit weight. As a result,the self-discharge is rendered somewhat prominent in thelithium-titanium composite oxide, compared with the conventionalmaterial.

It should be noted in this connection that γ-butyrolactone is likely tobe reduced, compared with the linear carbonate or the cyclic carbonate.To be more specific, the organic solvents are likely to be reduced inthe order of γ-butyrolactone>>>ethylene carbonate>propylenecarbonate>>dimethyl carbonate>methyl ethyl carbonate>diethyl carbonate.Incidentally, the degree of difference in the reactivity between thesolvents is denoted by the number of signs of inequality (>).

Such being the situation, in the case where the liquid electrolytecontains γ-butyrolactone, a good film can be formed on the surface ofthe lithium-titanium composite oxide even under the operable potentialregion of the lithium-titanium composite oxide. As a result, theself-discharge can be suppressed so as to improve the storagecharacteristics of the nonaqueous electrolyte battery under hightemperatures. This is also the case with the mixed solvents referred toabove.

In order to form a better protective film, it is desirable forγ-butyrolactone to be contained in an amount not smaller than 40% byvolume and not larger than 95% by volume of the organic solvent.

It is also possible to use an ionic liquid containing lithium ions, apolymer solid electrolyte, and an inorganic solid electrolyte as thenonaqueous electrolyte.

The ionic liquid denotes a compound, which can be present in the form ofa liquid material under room temperature (15° C. to 25° C.) and whichcontains an organic cation and an organic anion. The ionic liquid notedabove includes, for example, an ionic liquid that can be present singlyin the form of a liquid material, an ionic liquid that can be convertedinto a liquid material when mixed with an electrolyte, and an ionicliquid that can be converted into a liquid material when dissolved in anorganic solvent. Incidentally, the ionic liquid, which is used in thenonaqueous electrolyte battery, can have a melting point not higher than25° C. Also, the organic cation forming the ionic liquid in question canhave a quaternary ammonium skeleton.

The polymer solid electrolyte is prepared by dissolving an electrolytein a polymer material, followed by solidifying the resultant solution.

Further, the inorganic solid electrolyte denotes a solid materialexhibiting a lithium ion conductivity.

3) Positive Electrode

The positive electrode comprises a positive electrode current collectorand a positive electrode layer formed on one surface or both surfaces ofthe positive electrode current collector and containing a positiveelectrode active material, a positive electrode conductive agent and abinder.

The positive electrode active material includes, for example, an oxideand a polymer.

The oxides include, for example, manganese dioxide (MnO₂) absorbing Li,iron oxide, copper oxide, nickel oxide, a lithium-manganese compositeoxide such as Li_(x)Mn₂O₄ or Li_(x)MnO₂, a lithium-nickel compositeoxide such as Li_(x)NiO₂, a lithium-cobalt composite oxide such asLi_(x)CoO₂, a lithium-nickel-cobalt composite oxide such asLiNi_(1-y)Co_(y)O₂, a lithium-manganese-cobalt composite oxide such asLiMn_(y)Co_(1-y)O₂, the Spinel type lithium-manganese-nickel compositeoxide such as Li_(x)Mn_(2-y)Ni_(y)O₄, a lithium phosphate oxide havingan olivine structure such as Li_(x)FePO₄, Li_(x)Fe_(1-y)Mn_(y)PO₄, orLi_(x)CoPO₄, an iron sulfate such as Fe₂(SO₄)₃, and vanadium oxide suchas V₂O₅.

The polymer includes, for example, a conductive polymer material such aspolyaniline or polypyrrole, and a disulfide series polymer material. Itis also possible to use sulfur (S), a fluorocarbon, etc. as the positiveelectrode active material.

The positive electrode active material that is desirable includes, forexample, a lithium-manganese composite oxide (e.g., Li_(x)Mn₂O₄), alithium-nickel composite oxide (e.g., Li_(x)NiO₂), a lithium-cobaltcomposite oxide (e.g., Li_(x)CoO₂), a lithium-nickel-cobalt compositeoxide (e.g., Li_(x)Ni_(1-y)Co_(y)O₂), the Spinel typelithium-manganese-nickel composite oxide (e.g., Li_(x)Mn_(2-y)Ni_(y)O₄),a lithium-manganese-cobalt composite oxide (e.g.,Li_(x)Mn_(y)Co_(1-y)O₂), a lithium-nickel-cobalt-manganese compositeoxide (e.g., Li_(x)Ni_(1-y-z)Co_(y)Mn_(z)O₂) and lithium iron phosphate(e.g., Li_(x)FePO₄). The positive electrode active materials exemplifiedabove make it possible to obtain a high positive electrode voltage.Incidentally, it is desirable for each of the molar ratios x, y and z inthe chemical formulas given above to fall within a range of 0 to 1.

It is also desirable to use a compound represented byLi_(a)Ni_(b)Co_(c)Mn_(d)O₂, where the molar ratios a, b, c and d are0≦a≦1.1, 0.1≦b≦0.5, 0≦c≦0.9, and 0.1≦d≦0.5). Incidentally, Li and Co areoptional components of the compound given above. It is more desirablefor the molar ratios b, c and d in the structural formula given above tofall with the ranges of: 0.3≦b≦0.4, 0.3≦c≦0.4, and 0.3≦d≦0.4.

Since the positive electrode active materials exemplified above exhibita high ionic conductivity, the diffusion of the lithium ions within thepositive electrode active material is unlikely to provide therate-determining step when the positive electrode active material isused in combination with the negative electrode active materialspecified in this embodiment of the present invention so as to make itpossible to further improve the large current characteristics.

It is desirable for the positive electrode active material to have theprimary particle diameter not smaller than 100 nm and not larger than 1μm. If the primary particle diameter is not smaller than 100 nm, thepositive electrode active material can be handled easily in theindustrial manufacture of the nonaqueous electrolyte battery. On theother hand, if the primary particle diameter is not larger than 1 μm,the diffusion of the lithium ions within the particle can be proceededsmoothly.

It is desirable for the positive electrode active material to have aspecific surface area not smaller than 0.1 m²/g and not larger than 10m²/g. If the specific surface area of the positive electrode activematerial is not smaller than 0.1 m²/g, it is possible to securesufficiently the absorption-release sites of the lithium ions. On theother hand, if the specific surface area of the positive electrodeactive material is not larger than 10 m²/g, the positive electrodeactive material can be handled easily in the industrial manufacture ofthe nonaqueous electrolyte battery, and it is possible to secure asatisfactory charge-discharge cycle life of the nonaqueous electrolytebattery.

The positive electrode conductive agent permits enhancing the currentcollecting performance and also permits suppressing the contactresistance between the current collector and the active material. Thepositive electrode conductive agent includes, for example, acarbonaceous material such as acetylene black, carbon black andgraphite.

The binder for bonding the positive electrode active material to thepositive electrode conductive agent includes, for example,polytetrafluoroethylene (PTFE), polyvinylidene fluoride (PVdF) and afluorinated rubber.

Concerning the mixing ratio of the positive electrode active material,the positive electrode conductive agent, and the binder, it is desirablefor the mixing amount of the positive electrode active material to benot smaller than 80% by weight and not larger than 95% by weight, forthe mixing amount of the positive electrode conductive agent to be notsmaller than 3% by weight and not larger than 18% by weight, and for themixing amount of the binder to be not smaller than 2% by weight and notlarger than 17% by weight. If the positive electrode conductive agent ismixed in an amount not smaller than 3% by weight, it is possible toobtain the effects described above. On the other hand, if the mixingamount of the positive electrode conductive agent is not larger than 18%by weight, it is possible to suppress the decomposition of thenonaqueous electrolyte on the surface of the positive electrodeconductive agent during storage of the nonaqueous electrolyte batteryunder high temperatures. Further, where the binder is used in an amountnot smaller than 2% by weight, it is possible to obtain a sufficientelectrode strength. On the other hand, where the mixing amount of thebinder is not larger than 17% by weight, it is possible to decrease themixing amount of the insulator in the electrode so as to decrease theinternal resistance of the nonaqueous electrolyte battery.

It is desirable for the positive electrode current collector to beformed of an aluminum foil or an aluminum alloy foil containing at leastone element selected from the group consisting of Mg, Ti, Zn, Mn, Fe,Cu, and Si.

The positive electrode can be prepared by coating a positive electrodecurrent collector with a slurry prepared by, for example, suspending apositive electrode active material, a positive electrode conductiveagent and a binder in a suitable solvent, followed by drying the coatedslurry so as to form a positive electrode layer, and subsequentlypressing the positive electrode current collector having the positiveelectrode layer formed thereon. Alternatively, it is also possible toform a mixture of a positive electrode active material, a positiveelectrode conductive agent and a binder into pellets, which are used forforming the positive electrode layer.

4) Separator

The separator includes, for example, a porous film includingpolyethylene, polypropylene, cellulose and/or polyvinylidene fluoride(PVdF), and an unwoven fabric made of a synthetic resin. Particularly,it is desirable in view of the improvement in safety to use a porousfilm made of polyethylene or polypropylene because the particular porousfilm can be melted under a prescribed temperature so as to break thecurrent.

5) Case

The case is formed of a laminate film having a thickness of, forexample, 0 2 mm or less, or a metal sheet having a thickness of, forexample, 0.5 mm or less. It is more desirable for the metal sheet tohave a thickness of 0.2 mm or less. Also, the case has a flattenedshape, an angular shape, a cylindrical shape, a coin shape, a buttonshape or a sheet shape, or is of a laminate type. The case includes acase of a large battery mounted to, for example, an electric automobilehaving two to four wheels in addition to a small battery mounted to aportable electronic device.

The laminate film includes, for example, a multi-layered film includinga metal layer and a resin layer covering the metal layer. For decreasingthe weight of the battery, it is desirable for the metal layer to beformed of an aluminum foil or an aluminum alloy foil. On the other hand,the resin layer for reinforcing the metal layer is formed of a polymermaterial such as polypropylene (PP), polyethylene (PE), Nylon, andpolyethylene terephthalate (PET). The laminate film case can be obtainedby bonding the periphery of superposed laminate films by the thermalfusion.

It is desirable for the metal case to be formed of aluminum or analuminum alloy. Also, it is desirable for the aluminum alloy to be analloy containing an element such as magnesium, zinc or silicon. On theother hand, it is desirable for the amount of the transition metals,which are contained in the aluminum alloy, such as iron, copper, nickeland chromium, to be not larger than 100 ppm.

6) Negative Electrode Terminal

The negative electrode terminal is formed of a material exhibiting anelectrical stability and conductivity within the range of 1.0 V to 3.0 Vof the potential relative to the lithium ion metal. To be more specific,the material used for forming the negative electrode terminal includes,for example, aluminum and an aluminum alloy containing Mg, Ti, Zn, Mn,Fe, Cu or Si. In order to lower the contact resistance relative to thenegative electrode current collector, it is desirable for the negativeelectrode terminal to be formed of a material equal to the material usedfor forming the negative electrode current collector.

7) Positive Electrode Terminal

The positive electrode terminal is formed of a material exhibiting anelectrical stability and conductivity within the range of 3.0 V to 4.25V of the potential relative to the lithium ion metal. To be morespecific, the material used for forming the positive electrode terminalincludes, for example, aluminum and an aluminum alloy containing Mg, Ti,Zn, Mn, Fe, Cu or Si. In order to lower the contact resistance relativeto the positive electrode current collector, it is desirable for thepositive electrode terminal to be formed of a material equal to thematerial used for forming the positive electrode current collector.

The construction of the nonaqueous electrolyte battery according to thefirst embodiment of the present invention is not limited to that shownin FIGS. 1A and 1B. For example, it is possible for the nonaqueouselectrolyte battery according to the first embodiment of the presentinvention to be constructed as shown in FIGS. 5 and 6. To be morespecific, FIG. 5 is an oblique view, partly broken away, schematicallyshowing the construction of another flattened type nonaqueouselectrolyte secondary battery according to the first embodiment of thepresent invention, and FIG. 6 is a cross sectional view showing in amagnified fashion the construction in the circular portion B shown inFIG. 5.

As shown in FIG. 5, a laminate type electrode group 9 is housed in acase 8 formed of a laminate film. As shown in FIG. 6, the laminate typeelectrode group 9 comprises a positive electrode 3 and a negativeelectrode 4, which are laminated one upon the other with a separator 5interposed between the positive electrode 3 and the negative electrode4. Each of a plurality of positive electrodes 3 includes a positiveelectrode current collector 3 a and positive electrode layers 3 b formedon both surfaces of the positive electrode current collector 3 a andcontaining a positive electrode active material. Likewise, each of aplurality of negative electrodes 4 includes a negative electrode currentcollector 4 a and negative electrode layers 4 b formed on both surfacesof the negative electrode current collector 4 a and containing anegative electrode active material. One side of the negative electrodecurrent collector 4 a included in each negative electrode 4 protrudesfrom the positive electrode 3. The negative electrode current collector4 a protruding from the positive electrode 3 is electrically connectedto a band-like negative electrode terminal 2. The distal end portion ofthe band-like negative electrode terminal 2 is withdrawn from the case 8to the outside. Also, one side of the positive electrode currentcollector 3 a included in the positive electrode 3 is positioned on theside opposite to the protruding side of the negative electrode currentcollector 4 a and is protruded from the negative electrode 4, though theparticular construction is not shown in the drawing. The positiveelectrode current collector 3 a protruding from the negative electrode 4is electrically connected to a band-like positive electrode terminal 1.The distal end portion of the band-like positive electrode terminal 1 ispositioned on the side opposite to the side of the negative electrodeterminal 2 and is withdrawn from the side of the case 8 to the outside.

SECOND EMBODIMENT

A battery pack according to a second embodiment of the present inventioncomprises the nonaqueous electrolyte battery according to the firstembodiment of the present invention as a unit cell, and a plurality ofunit cells are included in the battery pack according to the secondembodiment of the present invention. The unit cells are arranged inseries or in parallel so as to form a battery module.

The unit cell according to the first embodiment of the present inventionis adapted for the preparation of the battery module. Also, the batterypack according to the second embodiment of the present invention isexcellent in its charge-discharge cycle characteristics as described inthe following.

In the lithium-titanium composite oxide, the phase having an irregularcrystal structure is increased with decrease in the crystallitediameter. As a result, the variation of the negative electrode potentialat the charge-discharge terminal and, thus, the variation of the batteryvoltage at the charge-discharge terminal, is rendered small so as todecrease the nonuniformity in the battery voltage in the battery module.It follows that the battery pack according to the second embodiment ofthe present invention can control the battery voltage easily to make itpossible to improve the charge-discharge cycle characteristics. Thenonuniformity in the battery voltage in the battery module is broughtabout due to the difference in capacity among the individual batteriesand tends to be rendered large when the battery module of a seriesconnection is fully charged.

An example of the battery pack according to the second embodiment of thepresent invention will now be described with reference to FIGS. 2 and 3.

FIG. 2 is an oblique view showing in a dismantled fashion theconstruction of the battery pack according to the second embodiment ofthe present invention.

As shown in FIG. 2, a plurality of plate-like unit cells 11, e.g., 8unit cells 11, are laminated one upon the other so as to form aparallelepiped laminate body 20 forming a battery module. As describedpreviously, each of the unit cells 11 is constructed such that thepositive electrode terminal 13 and the negative electrode terminal 14connected to the positive electrode and the negative electrode,respectively, are withdrawn to the outside of the case. A printed wiringboard 12 is arranged on the side toward which the positive electrodeterminal 13 and the negative electrode terminal 14 are allowed toprotrude.

The positive electrode terminal 13 is electrically connected to aconnector 16 on the side of the positive electrode via a wiring 15 onthe side of the positive electrode. Likewise, the negative electrodeterminal 14 is electrically connected to a connector 18 on the side ofthe negative electrode via a wiring 17 on the side of the negativeelectrode. The connectors 16, 18 on the side of the positive electrodeand the negative electrode, respectively, are connected to thecounterpart connectors mounted to the printed wiring board 12.

The laminate body 20 of the unit cells 11 is fixed by adhesive tapes 19.Protective sheets 21 each formed of rubber or a resin are arranged tocover the three side surfaces of the laminate body 20 except the sidetoward which protrude the positive electrode terminal 13 and thenegative electrode terminal 14. Also, a protective block 22 formed ofrubber or a resin is arranged in the clearance between the side of thelaminate body 20 and the printed wiring board 12.

The laminate body 20 is housed in a housing vessel 23 together with theprotective sheets 21, the protective block 22 and the printed wiringboard 12. Also, a lid 24 is mounted to close the upper open portion ofthe housing vessel 23.

Each constituent of the battery pack according to the second embodimentof the present invention will now be described in detail.

As shown in FIG. 3, a thermistor 25, a protective circuit 26, and aterminal 27 for the current supply to the external apparatus are mountedto the printed wiring board 12.

The thermistor 25 serves to detect the temperature of the unit cell 11.The signal denoting the detected temperature is transmitted to theprotective circuit 26.

As shown in FIG. 3, the protective circuit 26 is capable of breakingunder prescribed conditions wirings 28 a and 28 b stretched between theprotective circuit 26 and the terminal 27 for the current supply to theexternal apparatus. The prescribed conditions noted above include, forexample, the case where the temperature detected by the thermistor 25 ishigher than a prescribed temperature and the case of detecting, forexample, the over-charging, the over-discharging and the over current ofthe unit cell 11. In the case of detecting the individual unit cells 11,it is possible to detect the battery voltage, the positive electrodepotential or the negative electrode potential. Incidentally, in the caseof detecting the electrode potential, a lithium electrode used as areference electrode is inserted into the unit cell 11. In the case ofFIG. 3, the protective circuit 26 is provided with a battery voltagemonitoring circuit section. Each of the unit cells 11 is connected tothe battery voltage monitoring circuit section via a wiring 29.According to the particular construction, the battery voltage of each ofthe unit cells 11 can be detected by the protective circuit 26.Incidentally, FIG. 3 covers the case of applying the detection to theindividual unit cells 11. However, it is also possible to apply thedetection to the battery module 20. Further, in the case shown in FIG.3, all the unit cells 11 included in the battery module 20 are detectedin terms of voltage. Although it is particularly preferable that thevoltages of all of the unit cells 11 of the battery module 20 should bedetected, it may be sufficient to check the voltages of only some of theunit cells 11.

The battery pack according to the second embodiment of the presentinvention is excellent in the control of the positive electrodepotential or the negative electrode potential by the detection of thebattery voltage and, thus, is particularly adapted for the case wherethe protective circuit detects the battery voltage.

It is possible to use a thermally shrinkable tape in place of theadhesive tape 19. In this case, the protective sheets 21 are arranged onboth sides of the laminate body 20 and, after the thermally shrinkabletube is wound about the protective sheets 21, the thermally shrinkabletube is thermally shrunk so as to bond the laminate body 20.

Incidentally, FIG. 2 shows that the unit cells 11 are connected inseries. However, it is also possible to connect the unit cells 11 inparallel so as to increase the capacity of the battery pack. Of course,it is also possible to connect the assembled battery packs in series andin parallel.

The unit cell 11 used in the battery pack shown in FIGS. 2 and 3 isformed of the flattened type nonaqueous electrolyte battery shown inFIG. 1. However, the unit cells constituting the battery pack are notlimited to the nonaqueous electrolyte battery shown in FIG. 1. Forexample, it is also possible to use the flattened type nonaqueouselectrolyte battery shown in FIGS. 5 and 6 for forming the battery packaccording to the second embodiment of the present invention.

The construction of the battery pack can be changed appropriatelydepending on the use of the battery pack.

It is desirable for the battery pack according to the second embodimentof the present invention to be used in the field requiring the largecurrent characteristics and the charge-discharge cycle characteristics.To be more specific, it is desirable for the battery pack according tothe second embodiment of the present invention to be used in the powersource for a digital camera and for the vehicles such as the hybridelectric automobiles having two to four wheels, electric automobileshaving two to four wheels, and the assist bicycles.

Incidentally, where the nonaqueous electrolyte contains γ-butyrolactone(GBL) or a mixed solvent containing at least two organic solventsselected from the group consisting of propylene carbonate (PC), ethylenecarbonate (EC) and γ-butyrolactone (GBL), it is desirable for thebattery pack to be used in the field requiring the high temperaturecharacteristics, i.e., for the battery pack mounted to a vehicle.

The present invention will now be described with reference to Examplesof the present invention. Needless to say, the technical scope of thepresent invention is not limited to the following Examples as far as thesubject matter of the present invention is not exceeded.

<Rapid Charging Test>

Example 1

<Preparation of Positive Electrode>

In the first step, a slurry was prepared by adding 90% by weight of alithium-cobalt composite oxide (LiCoO₂) used as a positive electrodeactive material, 5% by weight of acetylene black used as a conductiveagent, and 5% by weight of polyvinylidene fluoride (PVdF) used as abinder to N-methyl pyrrolidone (NMP), followed by coating the bothsurfaces of an aluminum foil having thickness of 15 μm with theresultant slurry and subsequently drying and, then, pressing the currentcollector coated with the slurry so as to obtain a positive electrodehaving an electrode density of 3.3 g/cm³.

<Preparation of Lithium-Titanium Composite Oxide>

In the first step, an anatase type titanium oxide was put in a solutionprepared by dissolving lithium hydroxide, 0.0112 g of sodium hydroxideand 0.1336 g of potassium hydroxide in a pure water, followed bystirring and drying the reaction system. Further, the dried reactionsystem was baked under the air atmosphere at 780° C. for 10 hours so asto obtain a lithium-titanium composite oxide having a spinel structureand a chemical formula of Li₄Ti₅O₁₂ and containing 0.03% by weight of Naand 0.42% by weight of K. The crystallite diameter of thelithium-titanium composite oxide thus obtained was found to be 582 Å.

<Measurement of Crystallite Diameter and Strength Ratio of Main Peaks>

In the first step, the X-ray diffraction pattern using Cu-K α of thelithium-titanium composite oxide was obtained by using XRD (type numberM18XHF²²-SRA, manufactured by Mac Science Inc.). FIG. 4 exemplifies theX-ray diffraction pattern of the lithium-titanium composite oxide forthis Example. Incidentally, the X-ray diffraction pattern having thebackground and the K α₂ line removed therefrom was used in thesubsequent analysis.

The crystallite diameter was obtained by formula (1) given below(Scherrer formula) by calculating the half value width of the X-raydiffraction peak of the (111) plane of the diffraction angle (2 θ) of18° . Incidentally, for calculating the half value width of thediffraction peak, it is necessary to correct the line width that variesby the change of the optical system of the diffraction apparatus. Astandard silicon powder was used for this correction.

D _(hkl)=(K·λ)/(β·cos θ)  (1)

where D_(hkl) denotes the crystallite diameter (Å), λ denotes thewavelength (Å) of the X-ray used for the measurement, β denotes thebroadening of the diffraction angle, θ denotes the Bragg angle of thediffraction angle; and K denotes a constant (0.9).

The intensity ratio of main peaks of the anatase type TiO₂, the rutiletype TiO₂ and Li₂TiO₃, respectively, was calculated from the X-raydiffraction pattern on the basis that the peak intensity of main peak ofLi₄Ti₅O₁₂ was set at 100. Incidentally, the main peak of Li₄Ti₅O₁₂ was apeak at 4.83 Å (2 θ:18°). The main peak of the anatase type TiO₂ was apeak at 3.51 Å (2 θ:25°). The main peak of the rutile type TiO₂ was apeak at 3.25 Å (2 θ:27°). The main peak of Li₂TiO₃ was a peak at 2.07 Å(2 θ:43°).

<Manufacture of Negative Electrode>

A slurry was prepared by adding 90% by weight of the obtainedlithium-titanium composite oxide powder, which was used as the negativeelectrode active material, 5% by weight of coke baked at 1,200° C. (thelayer spacing d₀₀₂ of 0.3465 nm and the average particle diameter of 3μm), which was used as the negative electrode conductive agent, and 5%by weight of polyvinylidene fluoride (PVdF) used as a binder to N-methylpyrrolidone (NMP), followed by coating the both surfaces of an aluminumfoil having thickness of 15 μm, which was used as a negative electrodecurrent collector, with the resultant slurry, and subsequently dryingand, then, pressing the aluminum foil having the dried slurry layersformed thereon so as to obtain a negative electrode having an electrodedensity of 2.0 g/cm³.

Incidentally, the lithium-titanium composite oxide powder was found tohave an average particle diameter of 0.82 μm. The average particlediameter of the lithium-titanium composite oxide powder was measured asfollows.

Specifically, about 0.1 g of a sample, a surfactant, and 1 to 2 mL of adistilled water were put in a beaker, and the distilled water wassufficiently stirred, followed by pouring the stirred system in astirring water vessel. Under this condition, the light intensitydistribution was measured every 2 seconds and measured 64 times in totalby using SALD-300, which is a Laser Diffraction Particle Size Analyzermanufactured by Shimadzu Corporation, so as to analyze the particle sizedistribution data.

<Manufacture of Electrode Group>

A laminate structure was prepared by disposing a positive electrode, aseparator formed of a porous polyethylene film having a thickness of 25μm, a negative electrode and another separator one upon the other in theorder mentioned, followed by spirally winding the laminate structurethus prepared. The wound laminate structure was pressed under heat of90° C. so as to obtain a flattened electrode group having a width of 30mm and a thickness of 3.0 mm. The electrode group thus prepared washoused in a pack formed of a laminate film having a thickness of 0.1 mmand including an aluminum foil having a thickness of 40 μm and apolypropylene layer formed on each surface of the aluminum foil. Theelectrode group housed in the pack was subjected to a vacuum drying at80° C. for 24 hours.

<Preparation of Liquid Nonaqueous Electrolyte>

A liquid nonaqueous electrolyte was prepared by dissolving LiBF₄ used asan electrolyte in a mixed solvent prepared by mixing ethylene carbonate(EC) with γ-butyrolactone (GBL) in a mixing ratio by volume of 1:2. Theelectrolyte was dissolved in the mixed solvent in an amount of 1.5mol/L.

After the liquid nonaqueous electrolyte was poured into a laminate filmpack having the electrode group housed therein, the pack was perfectlyclosed by the heat seal so as to manufacture a nonaqueous electrolytesecondary battery constructed as shown in FIG. 1 and having a width of35 mm, a thickness of 3.2 mm and a height of 65 mm.

Examples 2 to 14 and Comparative Example 1

A nonaqueous electrolyte secondary battery was manufactured as inExample 1, except that the addition amounts of Na and K were set asshown in Table 1, and that used was a lithium-titanium composite oxidehaving the crystallite diameter shown in Table 1.

Examples 15 to 19

A nonaqueous electrolyte secondary battery was manufactured as inExample 1, except that the baking temperature was set as shown in Table1, and that used was a lithium-titanium composite oxide having thecrystallite diameter shown in Table 1.

Comparative Examples 2 to 8

A nonaqueous electrolyte secondary battery was manufactured as inExample 1, except that the baking temperature was set as shown in Table1, and that used was a lithium-titanium composite oxide having thecrystallite diameter shown in Table 1.

Examples 20 to 25

A nonaqueous electrolyte secondary battery was manufactured as inExample 1 and Examples 15 to 19, except that used wasLiNi_(1/3)Co_(1/3)Mn_(1/3O) ₂ as the positive electrode active material.

A rapid charging performance was evaluated in respect of the nonaqueouselectrolyte battery for each of Examples 1 to 25 and each of ComparativeExamples 1 to 8. To be more specific, the battery discharged to reachthe rated discharge voltage of 1.5 V under the current of 1 C wascharged for 3 hours under the constant voltage of 2.8 V. The obtainedcharging capacity was regarded as the standard charging capacity. Tables1 and 2 show the 80% charging time (seconds) required for charging 80%of the standard charging capacity.

Also, the electric capacity of the negative electrode was measured by ahalf cell test in which a lithium metal was used as the counterelectrode. To be more specific, lithium ions were absorbed (charging) inthe negative electrode under the current value of 0.1 mA/cm² to reach 1V(Li/Li⁺) with a lithium metal used for forming the counter electrode,followed by releasing the lithium ions (discharge) under the currentvalue of 0.1 mA/cm² to reach 2V (Li/Li⁺) with the counter electrode. Thedischarge capacity in this stage was converted into the capacity perunit weight of the negative electrode active material. The convertedvalue is also shown in Tables 1 and 2 as the negative electrodecapacity.

TABLE 1 Na K (Na + K) Main peak intensity ratio 80% Negative Bakingamount amount amount Crystallite Anatase Rutile charging electrodetemperature (% by (% by (% by diameter type type time capacity (° C.)weight) weight) weight) (Å) TiO₂ TiO₂ Li₂TiO₃ (seconds) (mAh/g) Example1 780 0.032 0.423 0.455 582 <1 <1 <1 109 167 Example 2 780 0.022 0.0740.096 694 <1 <1 <1 124 165 Example 3 780 0.028 0.074 0.102 688 <1 <1 <1121 164 Example 4 780 0.029 0.084 0.113 671 <1 <1 <1 120 165 Example 5780 0.040 0.087 0.127 601 <1 <1 <1 120 165 Example 6 780 0.033 0.2150.248 592 <1 <1 <1 117 165 Example 7 780 — 0.453 0.453 590 <1 <1 <1 112166 Example 8 780 0.080 0.696 0.776 578 <1 <1 <1 113 167 Example 9 7800.254 0.773 1.027 565 <1 <1 <1 106 167 Example 10 780 0.780 1.146 1.926551 <1 <1 <1 101 166 Example 11 780 1.254 1.052 2.306 545 <1 <1 <1 98165 Example 12 780 2.331 — 2.331 530 <1 <1 <1 92 166 Example 13 7800.893 1.920 2.813 529 <1 <1 <1 91 164 Example 14 780 1.021 2.023 3.044527 <1 <1 <1 91 160 Example 15 760 0.032 0.423 0.455 442 <1 2 2 68 167Example 16 740 0.032 0.423 0.455 313 <1 2 2 64 167 Example 17 720 0.0320.423 0.455 261 <1 3 3 61 166 Example 18 710 0.032 0.423 0.455 203 <1 53 64 164 Example 19 700 0.032 0.423 0.455 151 <1 7 3 69 163 Comparative780 0.012 0.028 0.040 1207 <1 <1 <1 1080 158 Example 1 Comparative 7600.012 0.028 0.040 1041 <1 2 2 892 158 Example 2 Comparative 740 0.0120.028 0.040 984 <1 4 4 471 157 Example 3 Comparative 720 0.012 0.0280.040 780 <1 5 6 333 156 Example 4 Comparative 700 0.012 0.028 0.040 7613 3 3 341 154 Example 5 Comparative 680 0.012 0.028 0.040 692 10 5 3 343149 Example 6 Comparative 600 0.012 0.028 0.040 435 20 7 4 353 109Example 7 Comparative 500 0.012 0.028 0.040 332 33 8 4 373 78 Example 8

The following description is based on the values obtained by applying anappropriate effective numeral to the numeral values shown in each ofTables 1 and 2.

The 80% charging time for Examples 1 to 19 is shorter than that forComparative Examples 1 to 8. The experimental data clearly support thatthe nonaqueous electrolyte battery according to the embodiment of thepresent invention is excellent in the rapid charging performance, i.e.,in the large current characteristics.

The 80% charging time for Examples 12 to 19 is shorter than that forExamples 1 to 11. The experimental data clearly support that, if thecrystallite diameter of the lithium-titanium composite oxide is notlarger than 5.3×10² Å, the nonaqueous electrolyte battery is made moreexcellent in the rapid charging performance, i.e., in the large currentcharacteristics.

The 80% charging time for Examples 15 to 19 is shorter than that forExamples 1 to 14. The experimental data clearly support that, if thecrystallite diameter of the lithium-titanium composite oxide is notlarger than 4.4×10² Å, the nonaqueous electrolyte battery is madefurthermore excellent in the rapid charging performance, i.e., in thelarge current characteristics.

The 80% charging time for Example 17 is shorter than that for Examples18 to 19. The experimental data clearly support that, if the main peakintensity of each of the rutile type TiO₂, the anatase type TiO₂ andLi₂TiO₃ is not larger than 3, the nonaqueous electrolyte battery is mademore excellent in the rapid charging performance, i.e., in the largecurrent characteristics.

Further, the crystallite diameter for Examples 1 to 19 is smaller thanthat for Comparative Example 1. The experimental data clearly supportthat, if the amount of (Na+K) is not smaller than 0.10% by weight andnot larger than 3.04% by weight based on the amount of thelithium-titanium composite oxide, the lithium-titanium composite oxidehaving the crystallite diameter not larger than 6.9×10² Å and small inthe amount of the impurity phase can be baked easily.

TABLE 2 Na K (Na + K) Main peak intensity ratio 80% Negative Bakingamount amount amount Crystallite Anatase Rutile charging electrodetemperature (% by (% by (% by diameter type type time capacity (° C.)weight) weight) weight) (Å) TiO₂ TiO₂ Li₂TiO₃ (seconds) (mAh/g) Example20 780 0.032 0.423 0.455 582 <1 <1 <1 87 167 Example 21 760 0.032 0.4230.455 442 <1 2 2 54 167 Example 22 740 0.032 0.423 0.455 313 <1 2 2 51167 Example 23 720 0.032 0.423 0.455 261 <1 3 3 48 166 Example 24 7100.032 0.423 0.455 203 <1 5 3 51 164 Example 25 700 0.032 0.423 0.455 151<1 7 3 55 163

The 80% charging time for Example 20 is shorter than that for Example 1.The experimental data clearly support that, in the case of using acompound represented by Li_(a)Ni_(b)Co_(c)Mn_(d)O₂ (where 0≦a≦1.1,0.1≦b≦0.5, 0≦c≦0.9, and 0.1≦d≦0.5) as the positive electrode activematerial, the nonaqueous electrolyte battery is rendered more excellentin the rapid charging performance, i.e., in the large currentcharacteristics.

This is also the case with each of Examples 21 to 25, as apparent fromthe comparison with Examples 15 to 19.

<High Temperature Storage Test>

Examples 26 to 29

A nonaqueous electrolyte secondary battery was manufactured as inExample 1, except that the solvent of the liquid electrolyte had acomposition shown in Table 3.

The nonaqueous electrolyte secondary battery for each of Example 1 andExamples 26 to 29 was stored under the fully charged state in a constanttemperature vessel maintained at 45° C., i.e., a constant temperaturevessel type No. EC-45 MTP manufactured by Hitachi Ltd. so as to measurethe remaining capacity after the storage for one month. Table 3 showsthe ratio of the remaining capacity of the nonaqueous electrolytesecondary battery to the discharge capacity before the storage.

TABLE 3 Remaining capacity/ Solvent discharge First Second ratiocapacity solvent/A solvent/B (A:B) (%) Example 1 EC GBL 1:2 97 Example26 EC PC 1:2 80 Example 27 EC DMC 1:2 74 Example 28 EC MEC 1:2 72Example 29 EC DEC 1:2 70

The remaining capacity for each of Examples 1 and 26 is larger than thatfor any of Examples 27 to 29. The experimental data clearly supportthat, in the case of using a mixed solvent containing at least twoorganic solvents selected from the group consisting of propylenecarbonate (PC), ethylene carbonate (EC) and γ-butyrolactone (GBL), it ispossible to improve the high temperature storage characteristics of thenonaqueous electrolyte secondary battery.

The remaining capacity for Example 1 is larger than that for any ofExamples 26 to 29. The experimental data clearly support that, in thecase of using a solvent containing γ-butyrolactone (GBL), it is possibleto improve further the high temperature storage characteristics of thenonaqueous electrolyte secondary battery.

Examples 30 to 33

A nonaqueous electrolyte secondary battery was manufactured as inExample 1, except that the solvent of the liquid electrolyte had acomposition shown in Table 4. Incidentally, the solvent ratio shown inTable 4 denotes the volume ratio of the solvent. The abbreviation ECshown in Table 4 denotes ethylene carbonate, GBL denotesγ-butyrolactone, PC denotes propylene carbonate, and VC denotes vinylenecarbonate.

The nonaqueous electrolyte secondary battery for each of Example 1,Example 26 and Examples 30 to 33 was stored under the fully chargedstate in a constant temperature vessel maintained at 60° C., i.e., aconstant temperature vessel type No. EC-45 MTP manufactured by HitachiLtd., so as to measure the remaining capacity after the storage for onemonth. Table 4 shows the ratio of the remaining capacity of thenonaqueous electrolyte secondary battery to the discharge capacitybefore the storage.

TABLE 4 Remaining First Second Third Fourth Solvent capacity/ solvent/solvent/ solvent/ solvent/ ratio discharge A B C D (A:B:C:D) capacityExample EC GBL — — 1:2 87 1 Example EC PC — — 1:2 70 26 Example EC GBLPC — 2:3:1 92 30 Example EC GBL PC — 1:1:1 90 31 Example EC GBL VC —1:2:0.05 92 32 Example EC GBL PC VC 2:3:1:0.05 94 33

As shown in Table 3 given previously, the high temperature storagecharacteristics of the nonaqueous electrolyte secondary battery underthe temperature of about 45° C. can be improved in Examples 1 and 26using two kinds of solvents selected from the group consisting of PC, ECand GBL. However, when it comes to the storage characteristics of thenonaqueous electrolyte secondary battery under a further highertemperature of 60° C., the secondary battery for Examples 30 to 33 usingat least three kinds of solvents selected from the group consisting ofPC, EC, GBL and VC is superior to the secondary battery for Examples 1and 26, as apparent from Table 4. The experimental data clearly supportthat, in order to obtain a sufficient high temperature storagecharacteristics, it is desirable to use at least three kinds of solventsselected from the group consisting of PC, EC, GBL and VC.

Additional advantages and modifications will readily occur to thoseskilled in the art. Therefore, the invention in its broader aspects isnot limited to the specific details and representative embodiments shownand described herein. Accordingly, various modifications may be madewithout departing from the spirit or scope of the general inventiveconcept as defined by the appended claims and their equivalents.

1. A nonaqueous electrolyte battery, comprising: a case; a positiveelectrode provided in the case; a negative electrode provided in thecase and containing a lithium-titanium composite oxide comprising acrystallite diameter not larger than 6.9×10² Å, the lithium-titaniumcomposite oxide satisfying that none of a main peak intensity of arutile type TiO₂, a main peak intensity of an anatase type TiO₂ and amain peak intensity of Li₂TiO₃ is larger than 7 when a main peakintensity of a lithium titanate having a spinel structure is determinedby the X-ray diffractometry and set at 100; and a nonaqueous electrolyteprovided in the case.
 2. The nonaqueous electrolyte battery according toclaim 1, wherein the crystallite diameter is not smaller than 1.5×10² Å.3. The nonaqueous electrolyte battery according to claim 1, wherein hecrystallite diameter is not smaller than 2.6×10² Å.
 4. The nonaqueouselectrolyte battery according to claim 1, wherein none of the main peakintensity of the rutile type TiO₂, the main peak intensity of theanatase type TiO₂ and the main peak intensity of Li₂TiO₃ is larger than3 when the main peak intensity of the lithium titanate is set at
 100. 5.The nonaqueous electrolyte battery according to claim 1, wherein thelithium-titanium composite oxide contains an element X consisting of atleast one of Na and K, and the amount of the element X contained in thelithium-titanium composite oxide is not smaller than 0.10% by weight andnot larger than 3.04% by weight.
 6. The nonaqueous electrolyte batteryaccording to claim 5, wherein the element X is positioned in a Li siteof lithium titanate.
 7. The nonaqueous electrolyte battery according toclaim 1, wherein the nonaqueous electrolyte contains at least two kindsof solvents selected from the group consisting of propylene carbonate,ethylene carbonate and γ-butyrolactone.
 8. The nonaqueous electrolytebattery according to claim 1, wherein the nonaqueous electrolytecontains γ-butyrolactone.
 9. The nonaqueous electrolyte batteryaccording to claim 1, wherein the nonaqueous electrolyte contains atleast three kinds of solvents selected from the group consisting ofpropylene carbonate, ethylene carbonate, γ-butyrolactone, and vinylenecarbonate.
 10. The nonaqueous electrolyte battery according to claim 1,wherein the positive electrode contains a compound represented byLi_(a)Ni_(b)Co_(c)Mn_(d)O₂, where 0≦a≦1.1, 0.1≦b≦0.5, 0≦c≦0.9 and0.1≦d≦0.5.
 11. The nonaqueous electrolyte battery according to claim 1,wherein the lithium-titanium composite oxide is in the form of particleshaving an average particle diameter not larger than 1 μm.
 12. A batterypack comprising nonaqueous electrolyte batteries, each of the nonaqueouselectrolyte batteries comprising: a case; a positive electrode providedin the case; a negative electrode provided in the case and containing alithium-titanium composite oxide comprising a crystallite diameter notlarger than 6.9×10² Å, the lithium-titanium composite oxide satisfyingthat none of a main peak intensity of a rutile type TiO₂, a main peakintensity of an anatase type TiO₂ and a main peak intensity of Li₂TiO₃is larger than 7 when a main peak intensity of a lithium titanate havinga spinel structure is determined by the X-ray diffractometry and set at100; and a nonaqueous electrolyte provided in the case.
 13. The batterypack according to claim 12, further comprising a protective circuitwhich detects a voltage of each of the nonaqueous electrolyte batteries.14. A vehicle comprising a battery pack defined in claim
 12. 15. Alithium-titanium composite oxide comprising a crystallite diameter notlarger than 6.9×10² Å and satisfying that none of a main peak intensityof a rutile type TiO₂, a main peak intensity of an anatase type TiO₂ anda main peak intensity of Li₂TiO₃ is larger than 7 when a main peakintensity of a lithium titanate having a spinel structure is determinedby the X-ray diffractometry and set at
 100. 16. The lithium-titaniumcomposite oxide according to claim 15, which is in the form of particleshaving an average particle diameter not larger than 1 μm.
 17. Thelithium-titanium composite oxide according to claim 15, wherein thecrystallite diameter is not smaller than 1.5×10² Å.
 18. Thelithium-titanium composite oxide according to claim 15, wherein none ofthe main peak intensity of the rutile type TiO₂, the main peak intensityof the anatase type TiO₂ and the main peak intensity of Li₂TiO₃ islarger than 3 when the main peak intensity of the lithium titanate isset at
 100. 19. The lithium-titanium composite oxide according to claim15, which contains an element X consisting of at least one of Na and K,and the amount of the element X contained in the lithium-titaniumcomposite oxide is not smaller than 0.10% by weight and not larger than3.04% by weight.
 20. The lithium-titanium composite oxide according toclaim 19, wherein the element X is positioned in a Li site of lithiumtitanate.